Biaxially textured articles formed by powder metallurgy

ABSTRACT

A biaxially textured alloy article having a magnetism less than pure Ni includes a rolled and annealed compacted and sintered powder-metallurgy preform article, the prefonn article having been formed from a powder mixture selected from the group of ternary mixtures consisting of: Ni powder, Cu powder, and Al powder, Ni powder, Cr powder, and Al powder; Ni powder, W powder and Al powder; Ni powder, V powder, and Al powder; Ni powder, Mo powder, and Al powder; the article having a fine and homogeneous grain structure; and having a dominant cube oriented {100}&lt;100&gt; orientation texture; and further having a Curie temperature less than that of pure Ni.

[0001] This invention was made with Government support under ContractNo. DE-AC05-96OR22464 awarded by the United States Department of Energy.The Government has certain rights in this invention.

CROSS-REFERENCE TO RELATED APPLICATIONS

[0002] The following relate to the present invention and are herebyincorporated by reference: U.S. Patent Application Docket No. 0316Method for Forming Biaxially Textured Articles by Powder Metallurgy byGoyal, filed on even date herewith; U.S. Pat. No. 5,739,086 StructuresHaving Enhanced Biaxial Texture and Method of Fabricating Same by Goyalet al., issued Apr. 14, 1998; U.S. Pat. No. 5,741,377 Structures HavingEnhanced Biaxial Texture and Method of Fabricating Same by Goyal et al.,issued Apr. 21, 1998; U.S. Pat. No. 5,898,020 Structures Having biaxialTexture and Method of Fabricating Same by Goyal et al., issued Apr. 27,1999; U.S. Pat. No. 5,958,599 Structures Having Enhanced Biaxial Textureby Goyal et al., issued Sep. 28, 1999, U.S. Pat. No. 5,964,966 Method ofForming Biaxially Textured Substrates and Devices Thereon by Goyal etal., issued Oct. 21, 1999; and U.S. Pat. No. 5,968,877 High Tc YBCOSuperconductor Deposited on Biaxially Textured Ni Substrate by Budai etal., issued Oct. 19, 1999.

FIELD OF THE INVENTION

[0003] The present invention relates to biaxially textured metallicsubstrates and articles made therefrom, and more particularly to suchsubstrates and articles made from high purity face-centered cubic (FCC)materials using powder metallurgy techniques to form long lengths ofbiaxially textured sheets, and more particularly to the use of saidbiaxially textured sheets as templates to grow epitaxialmetal/alloy/ceramic layers.

BACKGROUND OlF THE lNVENTION

[0004] Current materials research aimed at fabricating high-temperaturesuperconducting ceramics in conductor configurations for bulk, practicalapplications, is largely focused on powder-in-tube methods. Such methodshave proved quite successful for the Bi—(Pb)—Sr—Ca—Cu—O (BSCCO) familyof superconductors due to their unique mica-like mechanical deformationcharacteristics. In high magnetic fields, this family of superconductorsis generally limited to applications below 30 K. In the Re—Ba—Cu—O(ReBCO, Re denotes a rare earth element), Tl—(Pb,Bi)—Sr—(Ba)—Ca—Cu—O andHg—(Pb)—Sr—(Ba)—Ca—Cu—O families of superconductors, some of thecompounds have much higher intrinsic limits and can be used at highertemperatures.

[0005] It has been demonstrated that these superconductors possess highcritical current densities (J_(c)) at high temperatures when fabricatedas single crystals or in essentially single-crystal form as epitaxialfilms on single crystal substrates such as SrTiO₃ and LaAlO₃. Thesesuperconductors have so far proven intractable to conventional ceramicsand materials processing techniques to form long lengths of conductorwith J_(c) comparable to epitaxial films. This is primarily because ofthe “weak-link” effect.

[0006] It has been demonstrated that in ReBCO, biaxial texture isnecessary to obtain high transport critical current densities. HighJ_(c)'s have been reported in polycrystalline ReBCO in thin filmsdeposited on special substrates on which a biaxially texturednon-superconducting oxide buffer layer is first deposited using ion-beamassisted deposition (IBAD) techniques. IBAD is a slow, expensiveprocess, and difficult to scale up for production of lengths adequatefor many applications.

[0007] High J_(c)'s have also been reported in polycrystalline ReBCOmelt-processed bulk material which contains primarily small angle grainboundaries. Melt processing is also considered too slow for productionof practical lengths.

[0008] Thin-film materials having perovskite-like structures areimportant in superconductivity, ferroelectrics, and electro-optics. Manyapplications using these materials require, or would be significantlyimproved by, single crystal, c-axis oriented perovskite-like films grownon single-crystal or highly aligned metal or metal-coated substrates.

[0009] For instance, Y—Ba₂—Cu₃—O (YBCO) is an important superconductingmaterial for the development of superconducting current leads,transmission lines, motor and magnetic windings, and other electricalconductor applications. When cooled below their transition temperature,superconducting materials have no electrical resistance and carryelectrical current without heating up. One technique for fabricating asuperconducting wire or tape is to deposit a YBCO film on a metallicsubstrate. Superconducting YBCO has been deposited on polycrystallinemetals in which the YBCO is c-axis oriented, but not aligned in-plane.To carry high electrical currents and remain superconducting, however,the YBCO films must be biaxially textured, preferably c-axis oriented,with essentially no large-angle grain boundaries, since such grainboundaries are detrimental to the current-carrying capability of thematerial. YBCO films deposited on polycrystalline metal substrates donot generally meet this criterion.

[0010] The present invention provides a method for fabricating biaxiallytextured sheets of alloy substrates with desirable compositions. Thisprovides for applications involving epitaxial g$ devices on such alloysubstrates. The alloys can be thermal expansion and lattice parametermatched by selecting appropriate compositions. They can then beprocessed according to the present invention, resulting in devices withhigh quality films with good epitaxy and minimal microcracking.

[0011] The terms “process”, “method”, and “technique” are usedinterchangeably herein.

[0012] For further information, refer to the following publications:

[0013] 1. K. Sato, et al., “High-J_(c) Silver-Sheathed Bi-BasedSuperconducting Wires”, IEEE Transactions on Maanetics, 27 (1991) 1231.

[0014] 2. K. Heine, et al., “High-Field Critical Current Densities inBi₂Sr₂Ca₁Cu₂O_(8+x)/Ag Wires”, Applied Physics Letters, 55 (1991) 2441.

[0015] 3. R. Flukiger, et al., “High Critical Current Densities inBi(2223)/Ag tapes”, Superconductor Science & Technology 5, (1992) S61.

[0016] 4. D. Dimos et al., “Orientation Dependence of Grain-BoundaryCritical Currents in Y₁Ba₂Cu₃O_(7−*) Bicrystals”, Physical ReviewLetters, 61 (1988) 219.

[0017] 5. D. Dimos et al., “Superconducting Transport Properties ofGrain Boundaries in Y₁Ba₂Cu₃O₇ Bicrystals”, Physical Review B, 41 (1990)4038.

[0018] 6. Y. Iijima, et al., “Structural and Transport Properties ofBiaxially Aligned YBa₂Cu₃O_(7−x) Films on Polycrystalline Ni-Based Alloywith Ion-Beam Modified Buffer Layers”, Journal of Applied Physics, 74(1993) 1905.

[0019] 7. R. P. Reade, et al. “Laser Deposition of biaxially texturedYttria-Stabilized Zirconia Buffer Layers on Polycrystalline MetallicAlloys for High Critical Current Y—Ba—Cu—O Thin Films”, Applied PhysicsLetters, 61 (1992) 2231.

[0020] 8. D. Dijkkamp et al., “Preparation of Y—Ba—Cu OxideSuperconducting Thin Films Using Pulsed Laser Evaporation from High TcBulk Material,” Applied Physics Letters, 51, 619 (1987).

[0021] 9. S Mahajan et al., “Effects of Target and Template Layer on theProperties of Highly Crystalline Superconducting a-Axis Films ofYBa₂Cu₃O_(7−x) by DC-Sputtering,” Physica C, 213, 445 (1993).

[0022] 10. A. Inam et al., “A-axis Oriented EpitaxialYBa₂Cu₃O_(7−x)-PrBa₂Cu₃O_(7−x) Heterostructures,” Applied PhysicsLetters, 57, 2484 (1990).

[0023] 11. R. E. Russo et al., “Metal BufTer Layers and Y—Ba—Cu—O ThinFilms on Pt and Stainless Steel Using Pulsed Laser Deposition,” Journalof Applied Physics, 68, 1354 (1990).

[0024] 12. E. Narumi et al., “Superconducting YBa₂Cu₃O₆ ₈ Films onMetallic Substrates Using In Situ Laser Deposition,” Applied PhysicsLetters, 56, 2684 (1990).

[0025] 13. R. P. Reade et al., “Laser Deposition of Biaxially TexturedYttria-Stabilized Zirconia Buffer Layers on Polycrystalline MetallicAlloys for High Critical Current Y—Ba—Cu—O Thin Films,” Applied PhysicsLetters, 61, 2231 (1992).

[0026] 14. J. D. Budai et al., “In-Plane Epitaxial Alignment ofYBa₂Cu₃O_(7−x) Films Grown on Silver Crystals and Buffer Layers,”Applied Physics Letters, 62, 1836 (1993).

[0027] 15. T. J. Doi et al., “A New Type of Superconducting Wire;Biaxially Oriented Tl₁(Ba_(0.8)Sr_(0.2))₂Ca₂Cu₃O₉ on {100}<100> TexturedSilver Tape,” Proceedings of 7th International Symposium onSuperconductivity, Fukuoka, Japan, Nov. 8-11, 1994.

[0028] 16. D. Forbes, Executive Editor, “Hitachi Reports 1-meter Tl-1223Tape Made by Spray Pyrolysis”, Superconductor Week, Vol. 9, No. 8, Mar.6, 1995.

[0029]17. Recrystallization, Grain Growth and Textures, Papers presentedat a Seminar of the American Society for Metals, Oct. 16 and 17, 1965,American Society for Metals, Metals Park, Ohio.

OBJECTS OF THE INVENTION

[0030] Accordingly, it is an object of the present invention to providenew and useful biaxially textured metallic substrates and articles madetherefrom.

[0031] It is another object of the present invention to provide suchbiaxially textured metallic substrates and articles made therefrom byrolling and recrystallizing high purity face-centered cubic materials toform long lengths of biaxially textured sheets.

[0032] It is yet another object of the present invention to provide forthe use of said biaxially textured sheets as templates to grow epitaxialmetal/alloy/ceramic layers.

[0033] Further and other objects of the present invention will becomeapparent from the description contained herein.

SUMMARY OF THE INVENTION

[0034] In accordance with one aspect of the present invention, theforegoing and other objects are achieved by a biaxially textured alloyarticle having a magnetism less than pure Ni which comprises a rolledand annealed compacted and sintered powder-metallurgy preform article,the prefonn article having been formed from a powder mixture selectedfrom the group of binary mixtures consisting of: between 99 at % and 80at % Ni powder and between 1 at % and 20 at % Cr powder; between 99 at %and 80 at % Ni powder and between 1 at % and 20 at % W powder; between99 at % and 80 at % Ni powder and between 1 at % and 20 at % V powder;between 99 at % and 80 at % Ni powder and between 1 at % and 20 at % Mopowder; between 99 at % and 60 at % Ni powder and between 1 at % and 40at % Cu powder; between 99 at % and 80 at % Ni powder and between 1 at %and 20 at % Al powder; the article having a fine and homogeneous grainstructure; and having a dominant cube oriented {100}<100> orientationtexture; and further having a Curie temperature less than that of pureNi.

[0035] In accordance with a second aspect of the present invention, theforegoing and other objects are achieved by a biaxially textured alloyarticle having a magnetism less than pure Ni which comprises a rolledand annealed compacted and sintered powder-metallurgy preform article,the prefonn article having been formed from a powder mixture selectedfrom the group of ternary mixtures consisting of: Ni powder, Cu powder,and Al powder; Ni powder, Cr powder, and Al powder; Ni powder, W powderand Al powder; Ni powder, V powder, and Al powder; Ni powder, Mo powder,and Al powder; the article having a fine and homogeneous grainstructure; and having a dominant cube oriented {100}<100> orientationtexture; and further having a Curie temperature less than that of pureNi.

[0036] In accordance with a third aspect of the present invention, theforegoing and other objects are achieved by a biaxially textured alloyarticle alloy article having a magnetism less than pure Ni whichcomprises a rolled and annealed compacted and sintered powder-metallurgypreform article, the preform article having been formed from a powdermixture selected selected from the group of mixtures consisting of: atleast 60 at % Ni powder and at least one of Cr powder, W powder, Vpowder, Mo powder, Cu powder, Al powder, Ce powder, YSZ powder, Ypowder, and RE powder; the article having a fine and homogeneous grainstructure; and having a dominant cube oriented {100}<100> orientationtexture; and further having a Curie temperature less than that of pureNi.

[0037] In accordance with a fourth aspect of the present invention, theforegoing and other objects are achieved by a strengthened, biaxiallytextured alloy article having a magnetism less than pure Ni whichcomprises a rolled and annealed, compacted and sinteredpowder-metallurgy preform article, the prefonn article having beenformed from a powder mixture selected from the group of mixturesconsisting of: Ni, Ag, Ag—Cu, Ag—Pd, Ni—Cu, Ni—V, Ni—Mo, Ni—Al,Ni—Cr—Al, Ni—W—Al, Ni—V—Al, Ni—Mo—Al, Ni—Cu—Al; and at least one finepowder such as but not limited to A1 ₂O₃, MgO, YSZ, CeO₂, Y₂O₃; and YSZ;the article having a grain size which is fine and homogeneous andfurther having a domininant cube oriented {100}<100> orientationtexture; and further having a Curie temperature less than that of pureNi.

BRIEF DESCRIPTION OF THE DRAWINGS

[0038] In the drawings:

[0039]FIG. 1 shows a (111) pole figure for a Ni-9 at % W alloyfabricated by rolling and annealing a compacted and sintered, powdermetallurgy preform. The pole figure indicates only four peaks consistentwith only a well-developed {100}<100>, biaxial cube texture. The finalannealing temperature of the sample was 1200° C.

[0040]FIG. 2 shows a phi (φ) scan of the [111] reflection, with φvarying from 0° to 360°, for a Ni-9 at % W alloy fabricated by rollingand annealing a compacted and sintered, powder metallurgy preform. Thepresence of four peaks is with only a well-developed {100}<100>, biaxialcube texture is apparent. The final annealing temperature of the samplewas 1200° C. The FWHM of the φ-scan, as determined by fitting a gaussiancurve to one of the peaks is ˜8.8°. The FWHM of the peaks in this scanis indicative of the in-plane texture of the grains in the sample.

[0041]FIG. 3 shows a rocking curve (ω-scan) from 10° to 40° with thesample being rocked in the rolling direction, for a Ni-9 at % W alloyfabricated by rolling and annealing a compacted and sintered, powdermetallurgy preform. The final annealing temperature of the sample was1200° C. The peak is indicative of the out-of-plane texture of thesample. The FWHM of the ω-scan, as determined by fitting a gaussiancurve to one of the peaks is ˜6.1°.

[0042]FIG. 4 shows a rocking curve (ω-scan) from 10° to 40° with thesample being rocked about the rolling direction, for a Ni-9 at % W alloyfabricated by rolling and annealing a compacted and sintered, powdermetallurgy preform. The final annealing temperature of the sample was1200° C. The peak is indicative of the out-of-plane texture of thesample. The FWHM of the ω-scan, as determined by fitting a gaussiancurve to one of the peaks is ˜8.5°.

[0043]FIG. 5 shows a (111) pole figure for a Ni-9 at % W alloyfabricated by rolling and annealing a compacted and sintered, powdermetallurgy preform. The pole figure indicates only four peaks consistentwith only a well-developed {100}<100>, biaxial cube texture. The finalannealing temperature of the sample was 1400° C.

[0044]FIG. 6 shows a phi (φ) scan of the [111] reflection, with φvarying from 0° to 360°, for a Ni-9 at % W alloy fabricated by rollingand annealing a compacted and sintered, powder metallurgy preform. Thepresence of four peaks is with only a well-developed {100}<100>, biaxialcube texture is apparent. The final annealing temperature of the samplewas 1400° C. The FWHM of the φ-scan, as determined by fitting a gaussiancurve to one of the peaks is ˜5.8°. The FWHM of the peaks in this scanis indicative of the in-plane texture of the grains in the sample.

[0045]FIG. 7 shows a rocking curve (ω-scan) from 10° to 40° with thesample being rocked in the rolling direction, for a Ni-9 at % W alloyfabricated by rolling and annealing a compacted and sintered, powdermetallurgy preform. The final annealing temperature of the sample was1400° C. The peak is indicative of the out-of-plane texture of thesample. The FWHM of the ω-scan, as determined by fitting a gaussiancurve to one of the peaks is ˜4.3°.

[0046]FIG. 8 shows a rocking curve (ω-scan) from 10° to 40° with thesample being rocked about the rolling direction, for a Ni-9 at % W alloyfabricated by rolling and annealing a compacted and sintered, powdermetallurgy preform. The final annealing temperature of the sample was1400° C. The peak is indicative of the out-of-plane texture of thesample. The FWHM of the ω-scan, as determined by fitting a gaussiancurve to one of the peaks is ˜7.4°.

[0047]FIG. 9 shows a (111) pole figure for a Ni-13 at % Cr alloyfabricated by rolling and annealing a compacted and sintered, powdermetallurgy preform. The pole figure indicates only four peaks consistentwith only a well-developed {100}<100>, biaxial cube texture. The finalannealing temperature of the sample was 1200° C.

[0048]FIG. 10 shows a phi (φ) scan of the [111] reflection, with φvarying from 0° to 360°, for a Ni-13 at % Cr alloy fabricated by rollingand annealing a compacted and sintered, powder metallurgy ,, preform.The presence of four peaks is with only a well-developed {100}<100>,biaxial cube texture is apparent. The final annealing temperature of thesample was 1200° C. The FWHM of the φ-scan, as determined by fitting agaussian curve to one of the peaks is ˜8.7°. The FWHM of the peaks inthis scan is indicative of the in-plane texture of the grains in thesample.

[0049]FIG. 11 shows a rocking curve (ω-scan) from 10° to 40° with thesample being rocked in the rolling direction, for a Ni-13 at % Cr alloyfabricated by rolling and annealing a compacted and sintered, powdermetallurgy preform. The final annealing temperature of the sample was1200° C. The peak is indicative of the out-of-plane texture of thesample. The FWHM of the ω-scan, as b detenined by fitting a gaussiancurve to one of the peaks is ˜5.8°.

[0050]FIG. 12 shows a rocking curve (ω-scan) from 10° to 40° with thesample being rocked about the rolling direction, for a Ni-13 at % Cralloy fabricated by rolling and annealing a compacted and sintered,powder metallurgy preforn. The final annealing temperature of the samplewas 1200° C. The peak is indicative of the out-of-plane texture of thesample. The FWHM of the ω-scan, as determined by fitting a gaussiancurve to one of the peaks is ˜9.8°.

[0051]FIG. 13 shows a (111) pole figure for a Ni-13 at % Cr alloyfabricated by rolling and annealing a compacted and sintered, powdermetallurgy preform. The pole figure indicates only four peaks consistentwith only a well-developed {100}<100>, biaxial cube texture. The finalannealing temperature of the sample was 1400° C.

[0052]FIG. 14 shows a phi (φ) scan of the [111] reflection, with φvarying from 0° to 360°, for a Ni-13 at % Cr alloy fabricated by rollingand annealing a compacted and sintered, powder metallurgy preform. Thepresence of four peaks is with only a well-developed {100}<100>, biaxialcube texture is apparent. The final annealing temperature of the samplewas 1400° C. The FWHM of the φ-scan, as determined by fitting a gaussiancurve to one ofthe peaks is ˜6.1°. The FWHM of the peaks in this scan isindicative of the in-plane texture of the grains in the sample.

[0053]FIG. 15 shows a rocking curve (ω-scan) from 10° to 40° with thesample being rocked in the rolling direction, for a Ni-13 at % Cr alloyfabricated by rolling and annealing a compacted and sintered, powdermetallurgy preform. The final annealing temperature of the sample was1400° C. The peak is indicative of the out-of-plane texture of thesample. The FWHM of the ω-scan, as determined by fitting a gaussiancurve to one of the peaks is ˜4.5°.

[0054]FIG. 16 shows a rocking curve (ω-scan) from 10° to 40° with thesample being rocked about the rolling direction, for a Ni-13 at % Cralloy fabricated by rolling and annealing a compacted and sintered,powder metallurgy preform. The final annealing temperature of the samplewas 1400° C. The peak is indicative of the out-of-plane texture of thesample The FWHM of the ω-scan, as determined by fitting a gaussian curveto one of the peaks is ˜7.3°.

[0055]FIG. 17 shows a (111) pole figure for a Ni-0.03 at % Mg alloyfabricated by rolling and annealing a compacted and sintered, powdermetallurgy preform. The Mg is predominantly expected to be present asMgO. The pole figure indicates only four peaks consistent with only awell-developed {100}<100>, biaxial cube texture. The final annealingtemperature ofthe sample was 1200° C.

[0056]FIG. 18 shows a phi (φ) scan of the [111] reflection, with φvarying from 0° to 360°, for a Ni-0.03 at % Mg alloy fabricated byrolling and annealing a compacted and sintered, powder metallurgypreform The presence of four peaks is with only a well-developed{100}<100>, biaxial cube texture is apparent. The final annealingtemperature of the sample was 1200° C. The FWHM of the φ-scan, asdetermined by fitting a gaussian curve to one of the peaks is ˜7.7°. TheFWHM of the peaks in this scan is indicative of the in-plane texture ofthe grains in the sample.

[0057]FIG. 19 shows a rocking curve (ω-scan) from 10° to 40° with thesample being rocked in the rolling direction, for a Ni-0.03 at % Mgalloy fabricated by rolling and annealing a compacted and sintered,powder metallurgy preform. The final annealing temperature of the samplewas 1200° C. The peak is indicative of the out-of-plane texture of thesample. The FWHM of the ω-scan, as determined by fitting a gaussiancurve to one of the peaks is ˜7.8°.

[0058]FIG. 20 shows a rocking curve (ω-scan) from 10° to 40° with thesample being rocked about the rolling direction, for a Ni-0.03 at % Mg.The final annealing temperature of the sample was 1200° C. The peak isindicative of the out-of-plane texture of the sample. The FWHM of theω-scan, as determined by fitting, a gaussian curve to one of the peaksis ˜9.2°.

[0059]FIG. 21 shows a (111) pole figure for a Ni-9 at % W-0.03 at % Mgalloy fabricated by rolling and annealing a comnpacted and sintered,powder metallurgy preform. The Mg is predominantly expected to bepresent as MgO. The pole figure indicates only four peaks consistentwith only a well-developed {100}<100>, biaxial cube texture. The finalannealing temperature of the sample was 1200° C.

[0060]FIG. 22 shows a phi (φ) scan of the [111] reflection, with φvarying from 0° to 360°, for a Ni-9 at % W-0.03 % Mg alloy fabricated byrolling and annealing a compacted and sintered, powder metallurgyprefonn. The presence of four peaks is with only a well-developed{100}<100>, biaxial cube texture is apparent. The final annealingtemperature of the sample was 1200° C. The FWHM of the φ-scan, asdetermined by fitting a gaussian curve to one of the peaks is ˜9.1°. TheFWHM of the peaks in this scan is indicative of the in-plane texture ofthe grains in the sample.

[0061]FIG. 23 shows a rocking curve (ω-scan) from 10° to 40° with thesample being rocked in the rolling direction, for a Ni-9 at % W-0.03% Mgalloy fabricated by rolling and annealing a compacted and sintered,powder metallurgy preform. The final annealing temperature of the samplewas 1200° C. The peak is indicative of the out-of-plane texture of thesample. The FWHM of the ω-scan, as determined by fitting a gaussiancurve to one of the peaks is ˜7.2°.

[0062]FIG. 24 shows a rocking curve (ω-scan) from 10° to 40° with thesample being rocked about the rolling direction, for a Ni-9 at % W-0.03at % Mg alloy fabricated by rolling and annealing a compacted andsintered, powder metallurgy preform. The final annealing temperature ofthe sample was 1200° C. The peak is indicative of the out-of-planetexture of the sample. The FWHM of the ω-scan, as determined by fittinga gaussian curve to one of the peaks is ˜9.1°.

[0063]FIG. 25 shows a (111) pole figure for a Ni-9 at % W-0.03 at % Mgalloy fabricated by rolling and annealing a compacted and sintered,powder metallurgy preform. The Mg is predominantly expected to bepresent as MgO. The pole figure indicates only four peaks consistentwith only a well-developed {100}<100>, biaxial cube texture. The finalannealing temperature of the sample was 1400° C.

[0064]FIG. 26 shows a phi (φ) scan of the [111] reflection, with φvarying from 0° to 360°, for a Ni-9 at % W-0.03 at % Mg alloy fabricatedby rolling and annealing a compacted and sintered, powder metallurgypreform The presence of four peaks is with only a well-developed{100}<100>, biaxial cube texture is apparent. The final annealingtemperature of the sample was 1400° C. The FWHM of the φ-scan, asdetermined by fitting a gaussian curve to one of the peaks is ˜6.1°. TheFWHM of the peaks in this scan is indicative of the in-plane texture ofthe grains in the sample.

[0065]FIG. 27 shows a rocking curve (ω-scan) from 10° to 40° with thesample being rocked in the rolling direction, for a Ni-9 at % W-0.03 at% Mg alloy fabricated by rolling and annealing a compacted and sintered,powder metallurgy prefonn. The final annealing temperature of the samplewas 1400° C. The peak is indicative of the out-of-plane texture of thesample. The FWHM of the ω-scan, as determined by fitting a gaussiancurve to one of the peaks is ˜6.7°.

[0066]FIG. 28 shows a rocking curve (ω-scan) from 10° to 40° with thesample being rocked about the rolling direction, for a Ni-9 at % W-0.03at % Mg alloy fabricated by rolling and annealing a compacted andsintered, powder metallurgy preform. The final annealing temperature ofthe sample was 1400° C. The peak is indicative of the out-of-planetexture of the sample. The FWHM of the ω-scan, as determined by fittinga gaussian curve to one of the peaks is ˜7.5°.

[0067]FIG. 29 shows a (111) pole figure for a Ni-13 at % Cr-0.03 at % Mgalloy fabricated by rolling and annealing a compacted and sintered,powder metallurgy preform. The Mg is predominantly expected to bepresent as MgO. The pole figure indicates only four peaks consistentwith only a well-developed {100}<100>, biaxial cube texture. The finalannealing temperature of the sample was 1200° C.

[0068]FIG. 30 shows a phi (φ) scan of the [111] reflection, with φvarying from 0° to 360°, for a Ni-13 at % Cr-0.03 at % Mg alloyfabricated by rolling and annealing a compacted and sintered, powdermetallurgy preform. The presence of four peaks with only awell-developed {100}<100>, biaxial cube texture is apparent. The finalannealing temperature of the sample was 1200° C. The FWHM of the φ-scan,as determined by fitting a gaussian curve to one of the peaks is ˜8.1°.The FWHM of the peaks in this scan is indicative of the in-plane textureof the grains in the sample.

[0069]FIG. 31 shows a rocking curve (ω-scan) from 10° to 40° with thesample being rocked in the rolling direction, for a Ni-13 at % Cr-0.03at % Mg alloy fabricated by rolling and annealing a compacted andsintered, powder metallurgy preform. The final annealing temperature ofthe sample was 1200° C. The peak is indicative of the out-of-planetexture of the sample. The FWHM of the ω-scan, as determined by fittinga gaussian curve to one of the peaks is ˜5.1°.

[0070]FIG. 32 shows a rocking curve (ω-scan) from 10° to 40° with thesample being rocked about the rolling direction, for a Ni-13 at %Cr-0.03 at % Mg alloy fabricated by rolling and annealing a compactedand sintered, powder metallurgy prefonn. The final annealing temperatureof the sample was 1200° C. The peak is indicative of the out-of-planetexture of the sample. The FWHM of the ω-scan, as determined by fittinga gaussian curve to one of the peaks is ˜9.5°.

[0071]FIG. 33 shows a (111) pole figure for a Ni-13 at % Cr-0.03 at % Mgalloy fabricated by rolling and annealing a compacted and sintered,powder metallurgy preforn. The Mg is predominantly expected to bepresent as MgO. The pole figure indicates only four peaks consistentwith only a well-developed {100}<100>, biaxial cube texture. The finalannealing temperature of the sample was 1400° C.

[0072]FIG. 34 shows a phi (φ) scan of the [111] reflection, with φvarying from 0° to 360°, for a Ni-13 at % Cr-0.03 at % Mg alloyfabricated by rolling and annealing a compacted and sintered, powdermetallurgy preform. The presence of four peaks is with only awell-developed {100}<100>, biaxial cube texture is apparent. The finalannealing temperature of the sample was 1400° C. The FWHM of the φ-scan,as determined by fitting a gaussian curve to one of the peaks is ˜6.5°.The FWHM of the peaks in this scan is indicative of the in-plane textureof the grains in the sample.

[0073]FIG. 35 shows a rocking curve (ω-scan) from 10° to 40° with thesample being rocked in the rolling direction, for a Ni-13 at % Cr-0.03at % Mg alloy fabricated by rolling and annealing a compacted andsintered, powder metallurgy preform. The final annealing temperature ofthe sample was 1400° C. The peak is indicative of the out-of-planetexture of the sample. The FWHM of the ω-scan, as determined by fittinga gaussian curve to one of the peaks is ˜6.9°.

[0074]FIG. 36 shows a rocking curve (ω-scan) from 10° to 40° with thesample being rocked about the rolling direction, for a Ni-13 at %Cr-0.03 at % Mg alloy fabricated by rolling and annealing a compactedand sintered, powder metallurgy preform. The final annealing temperatureof the sample was 1400° C. The peak is indicative of the out-of-planetexture of the sample. The FWHM of the T)-scan, as determined by fittinga gaussian curve to one of the peaks is 7.9°.

DETAILED DESCRIPTION OF THE INVENTION

[0075] Note: As used herein, percentages of components in compositionsare atomic percent unless otherwise specified.

[0076] A new method for producing highly textured alloys has beendeveloped. It is well established in the art that high purity FCC metalscan be biaxially textured under certain conditions of plasticdeformation, such as rolling, and subsequent recrystallization. Forexample, a sharp cube texture can be attained by deforming Cu by largeamounts (90%) followed by recrystallization.

[0077] However, this is possible only in high purity Cu. Even smallamounts of impurity elements (i.e., 0.0025% P, 0.3% Sb, 0.18% Cd, 0.47%As, 1% Sn, 0.5% Be etc.) can significantly modify the b defonnationbehavior and hence the kind and amount of texture that develops ondeformation and recrystallization. In this invention, a method isdescribed to texture alloys of cubic materials, in particular FCC metalbased alloys. Alloys and composite compositions resulting in desirablephysical properties can be processed to forn long lengths of biaxiallytextured sheets. Such sheets can then be used as templates to growepitaxial metal/alloy/ceramic layers for a variety of 2; applications.

[0078] The present invention has application especially in the making ofstrengthened substrates with magnetism less than that of pure Ni. For asubstance to have less magnetism than pure Ni implies that its Curietemperature is less than that of pure Ni. Curie temperature is known inthe art as the temperature at which a metal becomes magnetic. In thefollowing description, a material having less magnetism than that ofpure Ni implies a material having a Curie temperature at least 50° C.less than that of pure Ni.

[0079] Many device applications require good control of the grainboundary of the materials comprising the device. For example in hightemperature superconductors grain boundary character is very important.The effects of grain boundary characteristics on current transmissionacross the boundary have been very clearly demonstrated for Y123. Forclean, stochiometric boundaries, J,(gb), the grain boundary criticalcurrent, appears to be determined primarily by the grain boundarymisorientation. The dependence of Jr((b) on misorientation angle hasbeen determined by Dimos et al. [1] in Y123 for grain boundary typeswhich can be formed in epitaxial films on bicrystal substrates. Theseinclude [001] tilt, [100] tilt, and [100] twist boundaries [1]. In eachcase high angle boundaries were found to be weak-linked. The low JCobserved in randomly oriented polycrystalline Y123 can be understood onthe basis that the population of low angle boundaries is small and thatfrequent high angle boundaries impede long-range current flow.

[0080] Recently, the Dimos experiment has been extended to artificiallyfabricated [001] tilt bicrystals in Tl₂Ba₂CaCu₂Ox [2], Tl₂Ba₂Ca₂Cu₃O[3],TlBa₂Ca₂Cu₂Ox [4], and Ndi.₈₅Ceo.l₅CuO₄ [3]. In each case it was foundthat, as in Y123, JC depends strongly on grain boundary misalignmentangle. Although no measurements have been made on Bi-2223, data oncurrent transmission across artificially fabricated grain boundaries inBi-2212 indicate that most large angle [001] tilt [3] and twist [5,6]boundaries are weak links, with the exception of some coincident sitelattice IA (CSL) related boundaries [5,6] It is likely that thevariation in JC with grain boundary misorientation in Bi-2212 andBi-2223 is similar to that observed in the well-characterized cases ofY123 and TI-based superconductors. Hence in order to fabricate hightemperature superconductors with very critical current densities, it isnecessary to biaxially align essentially ,F t all the grains. This hasbeen shown to result in significant improvement in the superconducting2SO, properties of YBCO films [7-10].

[0081] A method for producing biaxially textured substrates was taughtin previous U.S. Pat. Nos. 5,739,096, 5,741,377, 5,898,020, and5,958,599. That method relies on the ability to texture metals, inparticular FCC metals such as copper, to produce a sharp cube texturefollowed by epitaxial growth of additional metal/ceramic layers.Epitaxial YBCO films grown on such substrates resulted in high JC.However, in order to realize any applications, one of the areasrequiring significant improvement and modification is the nature of thesubstrate. The preferred substrate was made by starting with high purityNi, which is first thermoinechanically biaxially textured, followed byepitaxial deposition of metal and/or ceramic layers. Because Ni isferromagnetic, the substrate as a whole is mag,netic and this causesdifficulty in practical applications involving superconductors. A secondproblem is the thermal expansion mismatch between the preferredsubstrate and the oxide layers. The thermal expansion of the substrateis dominated by that of Ni which is quite different from most desiredceramic layers for practical applications. This mismatch can result incracking and may limit properties. A third problem is the limitation ofthe lattice parameter to that of Ni alone. If the lattice parameter canbe modified to be closer to that of the ceramic layers, epitaxy can beobtained far more easily with reduced internal stresses. This can reduceor prevent cracking and other stress-related defects and effects (e.g.delamination) in the ceramic films Although a method to form alloysstarting from the textured Ni substrate is also suggested in U.S. Pat.Nos. 5,739,086, 5,741,377, 5,898,020, and 5,958,599, its scope islimited in tenns of the kinds of alloys that can be fabricated. This isbecause only a limited set of elements can be homogeneously diffusedinto the textured Ni substrate. A method for fabricating textured alloyswas proposed in another previous invention U.S. Pat. No. 5,964,966. Theinvention involved the use of alloys of cubic metals such as Cu, Ni, Fe,Al and Ag for making biaxially textured sheets such that the stackingfault frequency, u, of the alloy with all the alloying additions is lessthan 0.009. In case it is not possible to make an alloy with desiredproperties to have the stacking fault frequency less than 0.009 at roomtemperature, then deformation can be carried out at higher temperatureswhere the u is less than 0.009. However, that invention may be limitedin the sharpness of the texture which can be attained. This is XQbecause no specific control on the starting material to fabricate thebiaxially textured alloys was given which results in a sharp biaxialtexture. Moreover, the alloys fabricated using the methods described inthe invention, result in materials which have secondaryrecrystallization temperatures less than 1200° C. Once the secondaryrecrystallization temperature is reached, the substrate essentiallybegins to lose all its cube texture. Low secondary recrystallizationtemperatures limit the sharpness of biaxial texture that can be obtainedand what deposition temperatures can be used for depositing epitaxialoxide or other layers on such substrates. Furthennore, the inventiondoes not teach how one could potentially texture and effectively use analloy with compositions such that the stacking fault frequency of thealloy is greater than 0.009 at room temperature. Lastly, the inventiondoes not provide a method or describe an article which effectivelyincorporates ceramic constituents in the alloy body to result in verysignificant mechanical toughening, yet maintaining the strong biaxialtexture. A metallic object such as a metal tape is defined as having acube texture when the [100} crystallographic planes of the metal arealigned parallel to the surface of the tape and the [100]crystallographic direction is aligned along the length of the tape. Thecube texture is referred to as the {100}<100> texture. Here, a newmethod for fabricating strongly or dominantly cube textured surfaces ofcomposites which have tailored bulk properties (i.e. thermal expansion,mechanical properties, non-magnetic nature, etc.) for the application inquestion, and which have a strongly textured surface that is compatiblewith respect to lattice parameter and chemical reactivity with thelayers of the electronic device(s) in question, is described. Herein theterm dominantly or strongly cube (ix tetured surface describes one thathas 95% of the grains comprising the surface in the {100}<100>orientation. oriented The method for fabricating biaxially texturedalloys of the herein disclosed and claimed invention utilizes powdermetallurgy technology. Powder metallurgy allows fabrication of alloyszip with homogeneous compositions everywhere without the detrimentaleffects of compositional segregation commonly encountered when usingvacuum melting or casting to make alloys. Furthermore, powder metallurgyallows easy control of the grain size of the starting alloy body.Moreover, powder metallurgy allows a fine and homogeneous grain size tobe achieved. Herein, fine grain size means grain size less than 200microns. Homogeneous grain size means variation in grain size of lessthan 40%. In the following we break the discussion into three parts:Procedures and examples to obtain biaxially textured alloys which havestacking fault frequencies less than 0.009 at room temperature, but havebetter biaxial textures and have higher secondary recrystallizationtemperatures. Procedures and examples to obtain biaxially texturedalloys with a distribution of ceramic particles for mechanicalstrengthening. Procedures and examples to obtain and effectively usebiaxially textured alloys which have stacking fault frequencies greaterthan 0.009 at room temperature.

PROCEDURES AND EXAMPLES TO OBTAIN BIAXIALLY TEXTURED ALLOYS WHICH HAVESTACKING FREQUENCIES LESS THAN 0.009 AT ROOM TEMPERATURE, BUT HAVEBETTER BIAXIAL TEXTURES AND HAVE HIGHER SECONDARY RECRYSTALLIZATIONTEMPERATURES

[0082] The basic premise or idea here is that alloys are fonned bystarting with high purity powders of the alloy constituents,mechanically mixing them together to fonn a homogeneous mixture, Fs>compacting and heat-treating the resulting body to form a raw article orstarting preform. The }H thennomechanical treatment results in a fineand home(,eneous orain size in the initial starting preform.

EXAMPLE I

[0083] Begin with a mixture of 80% Ni powder (99.99% purity) and 9% Wpowder. Mix and compact at appropriate pressures into a rod or billet.Then heat treat at 900° C. for 2 hr. The grain size at the end of heattreatment is less than 50 sum. Deform, by rolling, to a degree greaterthan 90% total deformation, preferably using 10% reduction per pass andby reversing the rolling direction during each subsequent pass. Annealat about 1200° C. for about 60 minutes to produce a sharp biaxialtexture. Annealing is perfonned in flowing 4% H₂ in Ar. FIG. I shows a(I I I ) X-ray diffraction pole figure of the biaxially textured alloysubstrate. As can be seen, only four peaks are evident. Each peak refersto one of four crystallographically similar orientations correspondingto {100}<100>, such that the (100) plane is parallel to the surface ofthe tape and <100>direction is aligned along the long axis of the tape.FIG. 2 shows a phi-scan of the [111] reflection showing the degree ofin-plane texture. The FWHM of the tape is determined by fitting agaussian curve to the data is 8.8°. FIG. 3 shows the rocking curve orthe out-of-plane texture as measured by scanning the [200] reflection ofthe substrate. FIG. 3 is a rocking curve with the sample being rocked inthe rolling direction and shows a FWHM of 6.14°. FIG. 4 is a rockingcurve with the sample being rocked about the rolling direction and showsa FWHM of 8.49°. This is truly a single orientation texture with allcrystallographic axis being aligned in all direction within 8-9°. Alloysmade by procedures other than what is described above result insecondary recrystallization at about 1200° C.

EXAMPLE II

[0084] Begin with a mixture of 80% Ni powder (99.99% purity) and 9% Wpowder. Mix and compact at appropriate pressures into a rod or billet.Then heat treat at 900° C. for 2 hr. The grain size at the end of heattreatment is less than 50 pm. Deform, by rolling, to a degree greaterthan 90% total deformation, preferably using 10% reduction per pass andby reversing the rolling direction during each subsequent pass. Annealat about 1400° C. for about 60 minutes to produce a sharp biaxialtexture. Annealing is performed in flowing 4% H₂ in Ar. FIG. 5 shows a(I 1I) X-ray diffraction pole figure of the biaxially textured alloysubstrate. As can be seen, only four peaks are evident. Each peak refersto one of four crystallographically similar orientations correspondingto {100}<100>, such that the (100) plane is parallel to the surface ofthe tape and <100>direction is aligned along the long axis of the tape.FIG. 6 shows a phi-scan of the [ I I ] reflection showing the degree ofin-plane texture. The FWHM of the tape is detenined by fitting agaussian curve to the data is 6.30. FIG. 7 shows the rocking curve orthe out-of-plane texture as measured by scanning the [200] reflection ofthe substrate. FIG. 7 is a rocking curve with the sample being rocked inthe rolling direction and shows a FWHM of 6.7°. FIG. 8 is a rockingcurve with the sample being rocked about the rolling direction and showsa FWHM of 7.50. This is truly a single orientation texture with allcrystallographic axis being aligned in all direction within 6-7° Alloysmade by procedures other than what is described above result insecondary recrystallization at temperatures much below 1400° C. and donot result in single orientation cube texture as shown in the polefigure of FIG. 5. EXAMPLE III Begin with a mixture of 87 at % Nickelpowder (99.99% purity) and 13% Chromium powder. Mix and compact atappropriate pressures into a rod or billet. Then heat treat at 900° C.for 2 hr. The grain size at the end of heat treatment is less than 50Fm. Deform, by rolling, to a degree ygreater than 90% total deformation,preferably using 10% reduction per pass and by reversing the rollingdirection during each subsequent pass. Anneal at about 1200° C. forabout 60 minutes to produce a sharp biaxial texture. Annealing isperformed in flowing 4% H₂ in Ar. FIG. 9 shows a (111) X-ray diffractionpole figure of the biaxially textured alloy substrate. As can be seen,only four peaks are evident. Each peak refers to one of fourcrystallographically similar orientations corresponding to 100,<100>,such that the (100) plane is parallel to the surface of the tape and<100> direction is aligned along the long axis of the tape. FIG. 10shows a phi-scan of the [I I I] reflection showing the degree ofin-plane texture. The FWHM of the tape determined by fitting a gaussiancurve to the data is 8.68°. FIG. 11 shows the : 5 rocking curve or theout-of-plane texture as measured by scanning the [200] reflection of thesubstrate. FIG. 11 is a rocking curve with the sample being rocked inthe rolling direction and shows a FWHM of 5.83°. FIG. 12 is a rockingcurve with the sample being rocked about the rolling direction and showsa FWHM of 9.820. This is truly a single orientation texture with all;9>. crystallographic axis being aligned in all directions within 8-10°.Alloys made by procedures 2{) other than what is described above resultin secondary recrystallization at 1200° C. EXAMPLE IV Begin with amixture of 87 at % Nickel powder (99.99% purity) and 13% Chromiumpowder. Mix and compact at appropriate pressures into a rod or billet.Then heat treat at 900° C. for 2 hr. The grain size at the end of heattreatment is less than 50 Em. Deform, by rolling, to a degree greaterthan 90% total deformation, preferably using 10% reduction per pass andby reversing the rolling direction during each subsequent pass. Annealat about 1400° C. for about 60 minutes to produce a sharp biaxialtexture. Annealing>is performed in flowing 4% H₂ in Ar. FIG. 13 shows a(111) X-ray diffraction pole figure of the biaxially textured alloysubstrate. As can be seen, only four peaks are evident. Each peak refersto one of four crystallographically similar orientations correspondingto {100}<100>, such that the (100) plane is parallel to the surface ofthe tape and <100> direction is aligned along the long axis of the tape.FIG. 14 shows a phi-scan of the [111] reflection showing the degree ofin-plane texture. The FWHM of the tape detennined by fitting a gaussiancurve to the data is 6.1°. FIG. 15 shows the rocking curve or theout-of-plane texture as measured by scanning the [200] reflection of thesubstrate. FIG. 15 is a rocking curve with the sample being rocked inthe rolling direction and shows a FWHM of 4.5°. FIG. 16 is a rockingcurve with the sample being rocked about the rolling direction and showsa FWHM of 7.3°. This is truly a single orientation texture with allcrystallographic axis being aligned in all directions within 6-7°.Alloys made by procedures other than the what is described above resultin secondary recrystallization at temperatures much below 1400° C. anddo not result in single orientation cube texture as shown in the polefigure of FIG. 13. SSimilar experiments can be performed with binaryalloys of Ni—Cu, Ni—V, Ni—Mo, Ni—Al, and with ternary alloys ofNi—Cr—mAl, Ni—W—Al, Ni—V—Al, Ni—Mo—Al, Ni—Cu—Al. Similar results arealso expected for 100% Ag and AO, alloys such Ag—Cu, Ag—Pd.

PROCEDURES AND EXAMPLES TO OBTAIN BIAXIALLY-TEXTURED ALLOYS WITH ADISTRIBUTION OF CERAMIC PARTICLES FOR MECHANICAL STRENGTHENING

[0085] Conventional wisdom and numerous experimental results indicatethat hard, ceramic particles are introduced or dispersed within a metalor alloy it results in significant mechanical strengthening. This arisesprimarily due to enhanced defect or dislocation generation should thismaterial be defonned. Conventional wisdom and prior experimental resultsalso indicate because of the presence of such hard, ceramic particles,and the enhanced defect generation locally at these particles, thedeformation is very inhomogeneous. Inhomogeneous deformation essentiallyprevents the formation of any sharp crystallographic texture. Hence,conventional wisdom and prior experimental results show that thepresence of even a very small concentration of ceramic particles resultin little texture fonnation even in high purity FCC metals such as Cuand Ni. Here we provide a method where ceramic particles can beintroduced in a homogeneous fashion to obtain mechanical strengtheningof the substrate, and still obtain a high degree of biaxial texture. Thekey is to have a particle size of less than lHm and uniform distributionof the ceramic particles in the final preform, prior to the finalrolling to obtain biaxial texture. EXAMPLE V Begin with a mixture of0.03 at % Mg and remaining Ni powder. Mix and compact at appropriatepressures into a rod or billet. Then heat treat at 900° C. for 2 hr.During this thennomechanical processing all the Mg is converted to MgOand it is dispersed in a fine and homogeneous manner throughout theprefonn. The grain size at the end of heat treatment is less than 50 Dm.Deform, by rolling, to a degree greater than 90% total deformation,preferably using 10% reduction per pass and by reversing the rollingdirection during each subsequent pass. Anneal at about 1200° C. forabout 60 minutes to produce a sharp biaxial texture. Annealing isperfonned in flowing t5 4 % H₂ in Ar.

[0086]FIG. 17 shows a (111) X-ray diffraction pole figure of thebiaxially textured, particulate, composite substrate. As can be seen,only four peaks are evident. Each peak refers to one of fourcrystallograplically sinilar- orientations corresponding to {100}<100>,such that the (100) 2i;W). plane is parallel to the surface of the tapeand <100> direction is aligned along the long axis of the tape. FIG. 18shows a phi-scan of the [111] reflection showing the degree of in-planetexture. The FWHM of the tape determined by fitting a gaussian curve tothe data is 8.68°. FIG. 19 shows the rocking curve or the out-of-planetexture as measured by scanning the [200] reflection of the substrate.FIG. 19 is a rocking curve with the sample being rocked in the rollingdirection and shows a FWHM of 7.920. FIG. 20 is a rocking curve with thesample being rocked about the rolling direction and shows a FWHM of9.20°. This is truly a single orientation texture with allcrystallographic axis being aligned in all directions within 8-10°.Alloy substrates made by procedures other than what is described aboveundergo secondary recrystallization at such annealing temperatures andlose most of their biaxial texture. On the contrary, the substratesreported here improve their biaxial textures upon annealing attemperatures as high as 1400° C. cl EXAMPLE VI

[0087] Begin with a mixture of 0.03 at % Mg, 9 at % W and remaining Nipowder. Mix and compact at appropriate pressures into a rod or billet.Then heat treat at 900° C. for 2 hr. During this thermomechanicalprocessing all the Mg is converted to MgO and it is dispersed in a fineand homogeneous manner throughout the preform. The grain size at the endof heat treatment is less than 50 Sm. Deform, by rolling, to a degreegreater than 90% total defonnation, preferably using 10% reduction perpass and by reversing the rolling direction during each subsequent pass.Anneal at about 1200° C. for about 60 minutes to produce a sharp biaxialtexture. Annealing is performed in flowing 4% H2 in Ar.

[0088]FIG. 21 shows a (11) X-ray diffraction pole figure of thebiaxially textured, particulate, S composite substrate As can be seen,only four peaks are evident. Each peak refers to one of fourcrystallographically similar orientations corresponding to 100<100>,such that the (100) plane is parallel to the surface of the tape and<100> direction is aligned along the long axis of the tape. FIG. 22shows a phi-scan of the [111] reflection showing the degree of in-planetexture. The FWHM of the tape determined by fitting a gaussian curve tothe data is 9.05°.

[0089]FIG. 23 shows the rocking curve or the out-of-plane texture asmeasured by scanning the [200] reflection of the substrate FIG. 23 is arocking curve with the sample being rocked in the rolling direction andshows a FWFM of 7.2°. FIG. 24 is a rocking curve with the sample beingrocked about the rolling direction and shows a FWHM of 9.040. This istruly a single orientation texture with all crystallographic axis beingaligned in all directions within 8-10°. Alloy substrates made byprocedures other than what is described above undergo secondaryrecrystallization at such annealing temperatures and lose most of theirbiaxial texture. On the contrary, the substrates reported here improvetheir biaxial textures upon annealing at temperatures as high as 140° C.

EXAMPLE VII

[0090] Begin with a mixture of 0.03 at % Mg, 9 at % W and remaining Nipowder (99.99% purity). Mix and compact at appropriate pressures into arod or billet. Then heat treat at 900° C. for 2 hr. During thisthermomechanical processing all the Mg is converted to MgO and it isdispersed in a fine and homogeneous manner throughout the preform. Thegrain size at the end of heat treatment is less than 50 uM. Deform, byrolling, to a degree greater than 90% total deformation, preferablyusing 10% reduction per pass and by reversing the rolling directionduring each subsequent pass. Anneal at about 1400° C. for about 60minutes to produce a sharp biaxial texture. Annealing is performed inflowing 4% H₂ in Ar. FIG. 25 shows a (111) X-ray diffraction pole figureof the biaxially textured alloy substrate. ‘Ar’ As can be seen, onlyfour peaks are evident. Each peak refers to one of fourcrystallographically similar orientations corresponding to {100}<100>,such that the (100) plane is parallel to the surface of the tape and<100> direction is aligned along the long axis of the tape. FIG. 26shows a phi-scan of the [111] reflection showing the degree of in-planetexture. The FWHM of the tape is deterinined by fitting a gaussian curveto the data is 6.1°. FIG. 27 shows the rocking curve or the out-of-planetexture as measured by scanning the [200] reflection of the substrate.FIG. 27 is a rocking curve with the sample being rocked in the rollingdirection and shows a FWHM of 6 7°. FIG. 28 is a rocking curve with thesample being rocked about the rolling direction and shows a FWHM of7.5°. This is truly a single orientation texture with allcrystallographic axis being aligned in all direction within 6-7°. Alloysubstrates made by procedures other than what is described above undergosecondary recrystallization at such annealing temperatures and lose mostof their biaxial texture. On the contrary, the substrates reported here,improve their biaxial textures upon annealing at temperatures as high as1400° C.

EXAMPLE VIII

[0091] Begin with a mixture of 0.03 at % Mg, 13 at % Cr and remaining Nipowder. Mix and compact at appropriate pressures into a rod or billet.Then heat treat at 900° C. for 2 hr. During this thermornechanicalprocessing all the Mg is converted to MgO and it is dispersed in a fineand homogeneous manner throughout the preform. The grain size at the endof heat treatment is less than 50 ktm. Deforn, by rolling,, to a degreegreater than 90% total defonnation, preferably using 10% reduction perpass and by reversing the rolling direction during each subsequent pass.Anneal at about 1200° C. for about 60 minutes to produce a sharp biaxialtexture. Annealing is performed in flowing 4% H₂ in Ar.

[0092]FIG. 29 shows a (11) X-ray diffraction pole figure of thebiaxially textured, particulate, composite substrate. As can be seen,only four peaks are evident. Each peak refers to one of fourcrystallographically similar orientations conresponding to {100}<100>,such that the (100) plane is parallel to the surface of the tape and<100> direction is aligned along the long axis of the tape. FIG. 30shows a phi-scan of the [111] reflection showing the degree of in-planetexture. The FWHM of the tape detennined by fitting a gaussian curve tothe data is 8.06°.

[0093]FIG. 31 shows the rocking curve or the out-of-plane texture asmeasured by scanning the [200] reflection of the substrate FIG. 31 is arocking curve with the sample being rocked in the rolling direction andshows a FWHM of 51° FIG. 32 is a rocking curve with the sample beingrocked about the rolling direction and shows a FWHM of 9.47°. This istruly a single orientation texture with all crystallographic axis beingaligned in all directions within 8-10°. Begin with a mixture of 0.03 at% Mg, 9 at % W and remaining Ni powder (99.99% purity). Mix and compactat appropriate pressures into a rod or billet. Then heat treat at 900°C. for 2 hr. During this thermomechanical processing all the Mg isconverted to MgO and it is dispersed in a fine and homogeneous mannerthroughout the prefoi. The rain size at the end of heat treatment isless than 50 pim. Deform, by rolling, to a degree greater than 90% totaldeformation, preferably using 10% reduction per pass and by reversing,the rolling direction during each subsequent pass. Anneal at about 1400°C. for about 60 minutes to produce a sharp biaxial texture. Annealing isperformed in flowing 4% H2 in Ar. EXAMPLE IX Begin with a mixture of0.03 at % Mg, 13 at % Cr and remaining Ni powder (99.99% purity). Mixand compact at appropriate pressures into a rod or billet. Then heattreat at 900° C. for 2 hr. During this thermornechanical processing allthe Mg is converted to MgO and it is dispersed in a fine and homogeneousmanner throLug(hout the prefonn. The grain size at the end of heattreatment is less than 50 pm. Deform, by rolling, to a degree greaterthan 90% total deformation, preferably using 10% reduction per pass andby reversing the rolling direction during each subsequent pass. Annealat about 1400° C. for about 60 minutes to produce a sharp biaxialtexture. Annealing is perfonned in flowing 4% H₂ in Ar.

[0094]FIG. 33 shows a (111) X-ray diffraction pole figure of thebiaxially textured alloy substrate. As can be seen, only four peaks areevident. Each peak refers to one of four crystallographically similarorientations corresponding to {100}<100>, such that the (100) plane isparallel to the surface of the tape and <100>direction is aligned alongthe long axis of the tape. FIG. 34 shows a phi-scan of the [11]reflection showing the degree of in-plane texture. The FWHM of the tapeis determined by fitting a gaussian curve to the data is 6.5°. FIG. 35shows the rocking curve or the out-of-plane texture as measured byscanning the [200] reflection of the substrate. FIG. 35 is a rockingcurve with the sample being rocked in the rolling direction and shows aFWHM of 6.90. FIG. 36 is a rocking curve with the sample being rockedabout the rolling direction and shows a FWHM of 7.9°. This is truly asingle orientation texture with all jig crystallographic axis beingaligned in all direction within 6-8°. Alloy substrates made byprocedures other than what is described above undergo secondaryrecrystallization at such annealing temperatures and lose most of theirbiaxial texture. On the contrary, the substrates reported here, improvetheir biaxial textures upon annealing at temperatures as high as 1400°C.

EXAMPLES X

[0095] Begin with 99.99% pure Ni powder, and mix in fine(nanocrystalline or microcrystalline) oxide powders such as CeO2, Y203,and the like. Mix homogeneously and compact to a monolithic form.Defonn, preferably by reverse rolling to a degree of deformnationgreater than 90%. Heat treat at temperatures above the primaryrecrystallization temperature but below the secondary recrystallizationtemperature to obtain a sharp biaxially textured substrate. Similarexperiments with additions of a dispersion and at least one fine metaloxide powder such as but not limited to A1 ₂ 0 ₃, MgO, YSZ, CeO₂, Y₂ 0₃., YSZ, and RE203; etc. can be performed with binary alloys of Ni—Cu,Ni—V, Ni—Mo, Ni—Al, and with ternary alloys of Ni—Cr—Al, Ni—W—Al,Ni—V—Al, Ni—Mo—Al, Ni—Cu—Al. Similar results are also expected for 100%Ag and Ag alloys such Ag—Cu, Ag—Pd.

PROCEDURES AND EXAMPLES TO OBTAIN AND EFFECTIVELY USE BIAXIALLY TEXTUREDALLOYS WHICH HAVE STACKING FAULT FREQUENCIES GREATER THAN 0.009 AT ROOMTEMPERATURE

[0096] In all the following examples, begin with separate powders of theconstituents required to form the alloy, mixing them thoroughly andcompacting them preferably into the form or a rod or billet. The rod orbillet is then deformed, preferably by rolling, at about roomtemperature or a higher temperature provided the higher temperature islow enough that negligible inter-diffusion of elements occurs. Duringthe initial stages of deformation the larger metal constituentessentially forms a connected and mechanically bonded network. The rodor billet is now rolled to a large degree of deformation, preferablygreater than 90%. The alloying element powders i remain as discreteparticles in the matrix and may not undergo any significant deformation.Once the deformation is complete, rapidly thermally re-crystallize thesubstrate to texture the matrix material The alloying elements can bediffused in at a higher temperature after the texture is attained in thematrix.

EXAMPLE XI

[0097] Begin with 80% Ni and 20% Cr powder. Mix homogeneously andcompact to a monolithic form. Heat-treat to low temperatures so as tobond Ni-Ni particles. Since Cr particles are completely surrounded byNi, their sintering or bonding to the Ni particles is not critical.Deform, preferably by reverse rolling to a degree of deformation greaterthan 90%. In such a case, the final substrate does not have ahomogeneous chemical composition. There are clearly Cr particlesdispersed in the matrix. The substrate is now rapidly heated in afurnace to a temperature between the primary and secondaryrecrystallization of Ni. The objective is to obtain a cube texture inthe Ni matrix, with local regions of high Cr concentrations. The aim ofthe heat treatment is to minimize diffusion of Cr into the Ni matrix.Once the cube texture has been obtained, desired epitaxial oxide,nitride or other buffer layers are deposited on the substrate. Once thefirst layer is deposited, the substrate can be heat treated at highertemperatures to affect diffusion of Cr into Ni. While highconcentrations of Cr of 20 at % in the substrate would result inappearance of secondary texture components, it does not matter at thispoint what the texture of the underlying metal below the texturedceramic buffer layer is, since further epitaxy is going to occur at thesurface of the first ceramic layer. Similar experiments can be perfonnedwith binary alloys of Ni—Cu, Ni—V, Ni—Mo, Ni—Al, and with ternary alloysof Ni—Cr—Al, Ni—W—Al, Ni—V—Al, Ni—Mo—Al, Ni—Cu—Al. Similar results arealso expected for 100% Ag and Ag alloys such Ag—Cu, Ag—Pd. Similarexperiments can also be performed with additions of a dispersion of atleast one fine metal oxide powder such as but not limited to A1 ₂ 0 ₃,MgO, YSZ, CeO₂, Y₂ 0 ₃,, YSZ, and RE203;etc. with binary alloys ofNi—Cu, Ni—V, Ni—Mo, Ni—Al, and with ternary alloys of Ni—Cr—Al, Ni—W—Al,Ni—V—Al, Ni—Mo—Al, Ni—Cu—Al. Similar results are also expected for 100%Ag and Ag alloys such Ag-Cu, Ag-Pd. While there has been shown anddescribed what are at present considered the preferred embodiments ofthe invention, it will be obvious to those skilled in the art thatvarious changes and modifications can be made therein without departingfrom the scope of the inventions defined by the appended claims

What is claimed is:
 1. A biaxially textured alloy article having amagnetism less than pure Ni comprising a rolled and annealed compactedand sintered poivder-metallurgy preform article, the preform articlehaving been formed from a powder mixture selected from the group ofternary mixtures consisting of: Ni powder, Cu powder, and Al powder; Nipowder, Cr powder, and Al powder; Ni powder, W powder and Al powder; Nipowder, V powder, and Al powder: Ni powder, Mo powder, and Al powder;the article having a fine and homogeneous grain structure; and having adominant cube oriented {100}<100> orientation texture; and furtherhaving a Curie temperature less than that of pure Ni.
 2. The biaxiallytextured article of claim 1 wherein the article maintains its{100}<100>texture at annealing temperatures up to 120° C.
 3. Thebiaxially, textured article of claim 1 wherein the article maintains its100<I 0>texture at annealing temperatures up to 100° C.
 4. The biaxiallytextured article of claim I wherein the article maintains its{100}<100>texture at annealing temperatures up to 1400° C.
 5. Thebiaxially textured alloy article of claim 1 further comprising at leastone of the group consisting of oxide layers and nitride lanersepitaxilally deposited onto at least a portion of the biaxially texturedsurface.
 6. The biaxially, textured alloy article of claim 1 furthercomprising at least one of the group consisting of electrical devicesand electro-optical devices deposited thereupon.
 7. The biaxiallytextured alloy article of claim 1 where in at least one layer hassuperconducting properties.